Pipeline and manufacturing method thereof

ABSTRACT

A pipeline is a pipeline having plural weld zones in which ends of plural steel pipes are joined by welding, the plural steel pipes are produced from plural charges of molten steel having one or more steel compositions; yield point elongation is not present on a stress-strain curve obtained when stress is applied in a longitudinal direction of each of the steel pipes; a thickness of each of the steel pipes t (mm) and an average pipe outside-diameter D (mm) satisfy t/Dx100≦6; and in the plurality of the weld zones, ΔYS which is a yield strength difference between one steel pipe and the other steel pipe that are welded to each other (MPa), and YR representing a yield ratio that is a ratio of the yield strength to tensile strength of a pipe having a low yield strength out of the one steel pipe and the other steel pipe, satisfy ΔYS≦−1.75×YR+230.

TECHNICAL FIELD OF THE INVENTION

The present invention relates to a pipeline which has a plurality of weld zones in which ends of a plurality of steel pipes are joined by welding, and a manufacturing method thereof.

Priority is claimed on Japanese Patent Application No. 2012-014991, filed on Jan. 27, 2012, and the content of which is incorporated herein by reference.

RELATED ART

When a pipeline is laid on the seabed, conventionally, a method of girth-welding steel pipes one by one on a vessel in a laying area, and sequentially sending the welded pipe to form a pipeline has been mainly used. However, in recent years, as a method of laying a pipeline, a spool method of forming a long pipe by girth-welding steel pipes in advance on land or on a vessel berthed at a steel pipe supply base, then, coiling the long pipe around a drum, transporting the pipe to the ocean where the pipeline is to be laid, and uncoiling the pipe on the ocean while laying a pipeline has been increasingly employed.

When the steel pipe is coiled on the drum, compressive strain occurs inside the coiling in a longitudinal direction of the steel pipe. In addition, outside the coiling, tensile strain occurs in a longitudinal direction of the steel pipe. The strain becomes the maximum compressive strain at an inner arc edge which is the innermost position of the coiling and becomes the maximum tensile strain at an outer arc edge which is the outermost position of the coiling. The magnitude of the strain is proportional to the diameter of the steel pipe and inversely proportional to the diameter of the drum. In a generally used steel pipe outside-diameter (for example, an outer diameter of 193.7 mm to 457.2 mm) and drum diameter (for example, a diameter of 16 m), a plastic strain of about 2% to 4% occurs at coiling in the inner arc edge and the outer arc edge. On the other hand, even when the steel pipe coiled around the drum is uncoiled on a vessel and is stretched linearly, similarly, a plastic strain of about 2% to 4% occurs in the steel pipe. In consideration of additional bending and unbending in the laying work, or bending in grounding on the seabed, it is necessary that the steel pipe and the girth-welded zone withstand three cycles of bending and unbending.

When the steel pipe is coiled around the drum, or when the steel pipe is uncoiled, the steel pipe and the vicinity of the girth-weld zone is excessively constricted or buckling occurs at the inner arc edge of the pipe body in the vicinity of the girth-weld zone in some cases. As a method of improving the bendability of the steel pipe, for example, in Patent Documents 1 and 2, there is disclosed a method of preventing softening of a heat affected zone of girth welding. In addition, for example, in Patent Documents 3, there is disclosed a method of decreasing the yield ratio of a steel pipe. Further, for example, in Patent Document 4, there is disclosed a method of limiting shape irregularity in a girth-weld zone.

PRIOR ART DOCUMENT Patent Document

[Patent Document 1] Japanese Unexamined Patent Application, First Publication No. H3-133576

[Patent Document 2] Japanese Unexamined Patent Application, First Publication No. H3-211255

[Patent Document 3] Japanese Unexamined Patent Application, First Publication No. 2001-192773

[Patent Document 4] Japanese Unexamined Patent Application, First Publication No. 2006-281217

DISCLOSURE OF THE INVENTION Problems to be Solved by the Invention

When the steel pipe is coiled around the drum and uncoiled from the drum, in order to improve the bending buckling resistance of the steel pipe so as not to cause buckling, the improvement of the work hardening properties of the steel pipe itself is effective. Then, in order to improve the work hardening properties of the steel pipe itself, decrease in the yield ratio (a ratio of yield strength to tensile strength) of the steel pipe is effective. However, the bending buckling resistance of the girth-weld zone is inferior to that of the steel pipe. Therefore, even when the work hardening properties of the steel pipe itself are improved, it is difficult to avoid buckling occurring at the inner arc edge of the pipe body of the steel pipe in the vicinity of the girth-weld zone. That is, even when the shape irregularity of the girth-weld zone is suppressed and further, the steel pipe having a low yield ratio is used, buckling occurs in the vicinity of the girth-weld zone.

The present invention has been made in consideration of the above problems. That is, an object of the present invention is to provide a pipeline in which deformation properties of a steel pipe (line pipe) is sufficiently exhibited. Here, the pipeline is formed by joining a plurality of steel pipes (line pipes).

Means for Solving the Problem

Even when the buckling resistance of the steel pipe itself is improved, buckling may occur in the vicinity of a weld zone of a welded joint zone where the steel pipes are joined with each other. It has been found that the buckling occurs not only in a zone affected by heat from welding, but also in a base metal portion which is not affected by heat in the welded joint zone.

Generally, the pipeline is laid over several kilometers or longer in many cases. The amount producible per melting charge is about 300 tons at most and thus, a steel pipe produced from plural pieces of molten steel is usually included in the pipeline. Even when the steel is melted so as to have the same chemical components, the ratio of each alloy element is changed within a target range. That is, there is a change between melting charges of the chemical components. In addition, even when the steel pipe is produced from the same molten steel, rolling conditions among the plural steel pipes are almost never completely identical. Therefore, even when the standard of each steel pipe used in the pipeline corresponds to the same standard, usually, there is a strength difference between the steel pipes in a predetermined range.

The inventors have paid attention to not only the yield ratio which represents the work hardening properties of a material, but also the strength difference between steel pipes that face each other in a girth-weld zone, and have conducted an intensive investigation into an influence on a buckling limitation of the steel pipe (a distance between a spool surface and an inner arc edge of the steel pipe at the time when wrinkles, that is, buckling is caused by greatly deforming the vicinity of the girth-weld zone of the inner arc edge). As a result, in a case where the difference in yield strength between the steel pipes is large, buckling occurs early even when, for example, the steel pipe has a low yield ratio. It has been newly found that in a case where the yield strength difference is small, buckling hardly occurs even when the steel pipe has a high yield ratio. That is, in order to obtain a pipeline in which the occurrence of buckling is suppressed over the entire length thereof, it is not sufficient only to control the production conditions of the steel pipe and it is necessary to carefully select steel pipes that face each other and weld the selected pipes in the production of the pipeline (in girth welding). In addition, since the pipeline is laid over a distance of several kilometers or longer as described above, it cannot be considered that steel pipes having a small yield strength difference over the entire length are welded unless steel pipes that face each other are intentionally selected and welded.

The present invention is made based on the above findings and the gist thereof is as follows.

(1) According to an aspect of the present invention, there is provided a pipeline which has a plurality of weld zones in which ends of a plurality of steel pipes are joined by welding, wherein: the plurality of the steel pipes are produced from a plurality of charges of molten steel having one or more steel compositions; a yield point elongation is not present on a stress-strain curve that is obtained when stress is applied in a longitudinal direction of each of the steel pipes; t which is a thickness of each of the steel pipes in units of mm and D which is an average pipe outside-diameter in units of mm satisfy a following Expression (a); and in the plurality of the weld zones, ΔYS which is a yield strength difference between one steel pipe and the other steel pipe that are welded to each other in units of MPa, and YR which represents a yield ratio that is a ratio of the yield strength to a tensile strength of a pipe having a low yield strength out of the one steel pipe and the other steel pipe, satisfy a following Expression (b).

t/D×100≦6  (a)

ΔYS≦−1.75×YR+230  (b)

(2) The pipeline according to (1) may further contain, as the steel compositions, by mass %, C: 0.04% or more and 0.15% or less, Mn: 1.0% or more and 1.75% or less, Nb: 0.005% or more and 0.10% or less, Ti: 0.005% or more and 0.02% or less, Al: 0.001% or more and 0.06% or less, Si: limited to 0.4% or less, P: limited to 0.015% or less, S: limited to 0.005% or less, N: limited to 0.007% or less, and a balance consisting of Fe and unavoidable impurities, a ΔCeq value which is an absolute value of a difference of Ceq values expressed by a following Expression (c) may be 0.045% or less between the one steel pipe and the other steel pipe, and the tensile strength of the plurality of the steel pipes may be 450 MPa to 850 MPa.

Ceq=[C]+[Mn]/6  (c)

Here, [C], and [Mn] represent C and Mn contents by mass %.

(3) The pipeline according to (2) may further contain, as the steel compositions, by mass %, one or more of Cu: 0.1% or more and 1.0% or less, Ni: 0.1% or more and 1.0% or less, Cr: 0.1% or more and 1.0% or less, Mo: 0.05% or more and 0.3% or less, and V: 0.01% or more and 0.1% or less, and the ΔCeq value may be expressed by Expression (d).

Ceq=[C]+[Mn]/6+([Ni]+[Cu])/15+([Cr]+[Mo]+[V])/5  (d)

Here, [C], [Mn], [Ni], [Cu], [Cr], [Mo], and [V] represent amounts of C, Mn, Ni, Cu, Cr, Mo, and V by mass %.

(4) According to another aspect of the present invention, there is provided a pipeline which has a plurality of weld zones in which ends of a plurality of steel pipes are joined by welding, wherein: the plurality of the steel pipes are produced from a plurality of charges of molten steel having one or more steel composition; a yield point elongation is present on a stress-strain curve that is obtained when stress is applied in a longitudinal direction of each of the steel pipes; t which is a thickness of each of the steel pipes in units of mm and D which is an average pipe outside-diameter in units of mm satisfy a following Expression (e); and in the plurality of the weld zones, ΔYS which is a yield strength difference between one steel pipe and the other steel pipe that are welded to each other in units of MPa, and YR which represents a yield ratio that is a ratio of the yield strength to tensile strength of one out of the one steel pipe and the other steel pipe having a low yield strength satisfy a following Expression (f).

t/D×100<6  (e)

ΔYS≦−0.69×YR+125  (f)

(5) The pipeline according to (4) may contain, as the steel compositions, by mass %, C: 0.04% or more and 0.15% or less, Mn: 1.0% or more and 1.75% or less, Nb: 0.005% or more and 0.05% or less, Ti: 0.005% or more and 0.02% or less, Al: 0.001% or more and 0.06% or less, Si: limited to 0.4% or less, P: limited to 0.015% or less, S: limited to 0.005% or less, N: limited to 0.007% or less, and a balance consisting of Fe and unavoidable impurities, a ΔCeq value which is an absolute value of a difference of Ceq values expressed by a following Expression (g) may be 0.045% or less between the one steel pipe and the other steel pipe, the tensile strength of the plurality of the steel pipes may be 450 MPa to 850 MPa, and front and rear surfaces of the plurality of the steel pipes may be coated with thermal process type resin.

Ceq=[C]+[Mn]/6  (g)

Here, [C], and [Mn] represent amounts of C and Mn by mass %.

(6) The pipeline according to (5) may further contain, as the steel compositions, by mass %, one or more of Cu: 0.1% or more and 1.0% or less, Ni: 0.1% or more and 1.0% or less, Cr: 0.1% or more and 1.0% or less, Mo: 0.05% or more and 0.3% or less, and V: 0.01% or more and 0.1% or less, and the ΔCeq value may be expressed by Expression (h).

Ceq=[C]+[Mn]/6+([Ni]+[Cu])/15+([Cr]+[Mo]+[V])/5  (h)

Here, [C], [Mn], [Ni], [Cu], [Cr], [Mo], and [V] represent amounts of C, Mn, Ni, Cu, Cr, Mo, and V by mass %.

(7) The pipeline according to (4) may contain, as the steel compositions, by mass %, C: 0.04% or more and 0.15% or less, Mn: 1.0% or more and 1.75% or less, Nb: 0.005% or more and 0.05% or less, Ti: 0.005% or more and 0.02% or less, Al: 0.001% or more and 0.06% or less, Si: limited to 0.4% or less, P: limited to 0.015% or less, S: limited to 0.005% or less, N: limited to 0.007% or less, and a remainder consisting of Fe and unavoidable impurities, a ΔCeq value which is an absolute value of a difference of Ceq values expressed by a following Expression (i) may be 0.045% or less between the one steel pipe and the other steel pipe, and the tensile strength of the plurality of the steel pipes may be 450 MPa or more and 850 MPa or less.

Ceq=[C]+[Mn]/6  (i)

Here, [C], and [Mn] represent amounts of C and Mn contents by mass %.

(8) The pipeline according to (7) may further contain, as the steel compositions, by mass %, at least one of Cu: 0.1% or more and 1.0% or less, Ni: 0.1% or more and 1.0% or less, Cr: 0.1% or more and 1.0% or less, Mo: 0.05% or more and 0.3% or less, and V: 0.01% or more and 0.1% or less, and the ΔCeq value may be expressed by Expression (j).

Ceq=[C]+[Mn]/6+([Ni]+[Cu])/15+([Cr]+[Mo]+[V])/5  (j)

Here, [C], [Mn], [Ni], [Cu], [Cr], [Mo], and [V] represent amounts of C, Mn, Ni, Cu, Cr, Mo, and V by mass %.

(9) According to still another aspect of the present invention, there is provided a method of producing the pipeline according to claim 1 including: a first yield strength measuring process in which the yield strength of the plurality of the steel pipes is measured; and a first welding process in which steel pipes in which the ΔYS satisfies the above Expression (b) are welded.

(10) According to still another aspect of the present invention, there is provided a method of producing the pipeline according to claim 1 including: a first assigning process in which production numbers capable of specifying each of the steel pipes are assigned to the plurality of the steel pipes in order of rolling; and a second welding process in which steel pipes produced from the same molten steel and the same hot-rolled coil and having a difference between the production numbers of 1 or more and 5 or less are weld.

(11) According to still another aspect of the present invention, there is provided a method of producing the pipeline according to claim 4 including: a second yield strength measuring process in which the yield strength of the plurality of the steel pipes is measured; and a third welding process in which steel pipes in which the ΔYS satisfies the above Expression (f) are welded.

(12) According to still another aspect of the present invention, there is provided a method of producing the pipeline according to claim 4 including: a second assigning process in which production numbers capable of specifying each of the steel pipes are assigned to the plurality of the steel pipes in order of rolling; and a forth welding process in which steel pipes produced from the same molten steel and the same hot-rolled coil and having a difference between the production numbers of 1 or more and 5 or less are welded.

Effects of the Invention

According to the present invention, it is possible to provide the pipeline in which the deformation properties of the steel pipe can be sufficiently exhibited and thus, the present invention very remarkably contributes to the industry.

BRIEF DESCRIPTION OF THE DRAWING

FIG. 1 is a view showing a state in which a steel pipe floats on an outer surface of a drum and illustrating a gap ΔC and strain occurring at an inner arc edge of the steel pipe.

FIG. 2 is a view showing a relationship between the gap ΔC and the maximum strain occurring at the inner arc edge of the steel pipe.

FIG. 3 is a view showing a relationship between a yield strength difference ΔYS and a yield ratio YR of steel pipes to be girth-welded.

FIG. 4 is a view illustrating a testing apparatus which imparts a bending moment to the end of the steel pipe.

FIG. 5A is a view showing an example of a method of producing the pipeline according to the embodiment.

FIG. 5B is a view showing another example of the method of producing the pipeline according to the embodiment.

EMBODIMENTS OF THE INVENTION

Hereinafter, a pipeline according to an embodiment of the present invention (hereinafter, referred to as a pipeline according to an embodiment in some cases) will be described with reference to the drawings. As shown in FIG. 1, a pipeline 1 has a joint structure in which the ends of plural steel pipes 2 are joined by welding. In the joint structure in which the ends of the steel pipes are welded to each other, one steel pipe 2 is set to a steel pipe A and the other steel pipe 2 is set to a steel pipe B for the sake of description. The ends of the steel pipe A and the steel pipe B are abutted against each other and joined at a weld zone 3 by full-circled welding. The length of the pipeline according to the embodiment is increased by joining a plurality of steel pipes in the above-described manner.

When the pipeline 1 according to the embodiment is laid on the seabed in a spool method, as show in FIG. 1, the pipeline 1 is coiled around a drum 4, transported to the ocean where the pipeline is to be laid, and uncoiled at the site to lay the pipeline 1 on the seabed. When the steel pipe is coiled around the drum 4, at an inner arc edge that is the innermost position of the coiling, the maximum compressive strain occurs in a longitudinal direction of the pipeline 1 (steel pipe 2). In addition, at an outer arc edge that is the outermost position of the coiling, the maximum tensile strain occurs in the longitudinal direction of the pipeline 1 (steel pipe 2). In particular, buckling may occur at the inner arc edge in a base metal portion of the welded joint zone, particularly, in the vicinity of a heat affected zone (HAZ) 5 of a weld zone 3.

When the length of the pipeline 1 is increased, the pipeline 1 is coiled around the drum 4 many times. However, since the largest strain occurs in the pipeline coiled on the innermost side, in the embodiment, the behavior of the pipeline coiled on the innermost side will be described.

First, the inventors have attempted a numerical analysis simulation by finite element analysis (FEA) to clarify a buckling mechanism when the pipeline 1 (steel pipe 2) is coiled around the drum 4 as shown in FIG. 1. In the analysis, the yield ratio YR of the steel pipe A and the steel pipe B were set to 85%, 92.5%, 95%, or 98%. In addition, the difference ΔYS between the yield strength of the steel pipe A and the yield strength of the steel pipe B was set to 0 MPa, 50 MPa, 75 MPa, or 100 MPa. Then, each yield ratio YR and each yield strength difference ΔYS were combined to perform analysis.

When the pipeline 1 (steel pipe 2) is coiled around the drum 4 as shown in FIG. 1, the compressive strain occurring in the heat affected zone inside of the coiling and the tensile strain occurring in the heat affected zone outside of the coiling may cause the pipeline 1 (steel pipe 2) to float on the outer surface of the drum 4 in the weld zone 3 in some cases. In this case, a gap ΔC is generated between the inner arc edge (inner surface) of the pipeline 1 (steel pipe 2) and the outer surface of the drum 4. The inventors have paid attention to the gap ΔC to investigate buckling that occurs at the inner arc edge.

The inventors have observed a relationship between the gap ΔC and the maximum strain max occurring at the inner arc edge when the thickness t (mm) and the average pipe outside-diameter D (mm) of the steel pipe are within the range of t/D×100≦6. As a result, as shown in FIG. 2, regardless of the magnitude (combination) of the yield ratio YR and the yield strength difference ΔYS, when the gap ΔC exceeds 20 mm, the value of the gap ΔC rapidly increases. That is, it has been found that local buckling occurs. The limit value of the gap ΔC, in which buckling occurs, was about 20 mm in both a steel pipe (a so-called “round type” steel pipe) in which yield point elongation does not appear on a stress-strain curve (SS curve) obtained when stress is applied in the longitudinal direction and a steel pipe (a so-called “YPE type” steel pipe) in which yield point elongation appears on a stress-strain curve obtained when stress is applied in the longitudinal direction. On the other hand, it has been clear that a larger local buckling strain occurs in the round type steel pipe than in the YPE type steel pipe, and the round type steel pipe is hardly buckled.

Next, the inventors have investigated a relationship between the yield strength difference ΔYS and the yield ratio YR when the gap ΔC reaches 20 mm. As a result, as shown in FIG. 3, it has been found that the yield strength difference ΔYS and the yield ratio YR have a proportional relationship. In addition, FIG. 3 shows a relationship between the yield ratio YR and the yield strength difference ΔYS of one (A or B) of the steel pipe A and the steel pipe B having a low yield strength. As seen from FIG. 3, it has been clear that the relationship between the yield ratio YR and the yield strength difference ΔYS in the round type steel pipe is different from the relationship between the yield ratio YR and the yield strength difference ΔYS in the YPE type steel pipe. That is, the graph in FIG. 3 shows that local buckling can be prevented from occurring by controlling the relationship between the yield strength difference ΔYS between the steel pipe A and the steel pipe 13 and the yield ratio YR of a steel pipe (A or B) having a low yield strength in a pipeline formed of steel pipes (round type steel pipes) having a round type SS curve so as to satisfy the following Expression (b).

ΔYS≦−1.75×YR+230  (b)

On the other hand, it is found that local buckling can be prevented from occurring in a pipeline formed of steel pipes having a YPE type SS curve by controlling the relationship between the yield strength difference ΔYS between the steel pipe A and the steel pipe B and the yield ratio YR of a steel pipe (A or B) having a low yield strength so as to satisfy the following Expression (f).

ΔYS≦−0.69×YR+125  (f)

For the purpose of improving corrosion resistance or the like, even when a steel pipe using a steel sheet whose front and rear surface are coated with a thermal process type resin is used, the relationship of the above Expression (f) is satisfied.

In the pipeline according to the embodiment, local buckling can be prevented from occurring over the entire length regardless of the components or the strength of the steel pipe such that steel pipes that face each other satisfy the above relationship (when the steel pipe is a round type, Expression (b) is satisfied, and when the steel pipe is a YPE type, Expression (f) is satisfied.

However, when properties suitable for practical use (for example, properties which satisfy X42 to X80 defined by American Petroleum Institute (API) SPECIFICATION 5L) are obtained, it is preferable to control each steel pipe as follows.

In the steel pipe (hereinafter, referred to as the steel pipe according to the embodiment in some cases) used in the pipeline according to the embodiment, a preferable chemical component range will be described. Here, in the pipeline, a plurality of charges of molten steel is used, but it is preferable that all the molten steel be within the following range. “%” in the content of each element means “mass %”.

C: 0.04% or more and 0.15% or less C is an element which contributes to the strengthening of the steel (steel pipe) and the content is preferably 0.04% or more. On the other hand, when C is excessively contained, toughness and weldability are deteriorated, and thus, the upper limit is preferably 0.15%. A more preferable range is 0.05% or more and 0.10% or less.

Mn: 1.0% or More and 1.75% Less

Mn is an element which increases hardenability and contributes to the strengthening of the steel, and the content is preferably 1.0% or more. On the other hand, Mn is an element which is easily segregated and when Mn is excessively contained, coarse MnS is formed at the center portion of the sheet thickness and thus, the properties may be deteriorated. Therefore, the upper limit of the Mn content is preferably 1.75%. A more preferable range is 1.0% or more and 1.6% or less.

Nb: 0.005% or More and 0.10% or Less

Nb is an element which facilitates refinement as a hot-rolled state by suppressing recrystallization during hot rolling (in a state in which subsequent processes such as heat treatment are not performed after hot rolling). In addition, Nb is an element which forms carbonitrides and contributes to the refinement and strengthening of the structure. In order to obtain the effects, the Nb content is preferably 0.005% or more. On the other hand, when Nb is excessively contained, carbonitrides are coarsened and the properties may be deteriorated. Therefore, the Nb content is preferably 0.10% or less. The content is more preferably 0.06% or less.

Ti: 0.005% or More and 0.02% or Less

Ti is an element which forms nitrides, fixes N and contributes to the refinement and strengthening of the structure. In order to obtain the effects, the Ti content is preferably 0.005% or more. On the other hand, when Ti is excessively added, coarse TiN is formed and the properties may be deteriorated. Therefore, the upper limit of the Ti content is preferably 0.02%.

Al: 0.001% or More and 0.06% or Less

Al is an effective element as a deoxidizing agent. In order to obtain a deoxidation effect, the Al content is preferably 0.001% or more. On the other hand, even when 0.06% or more of Al is added, the above effect is saturated and the steel is rather embrittled. Therefore, when Al is contained, the Al content is preferably 0.001% or more and 0.06% or less. The lower limit of the Al content is more preferably 0.01% or more.

Si: 0.4% or Less

Si is an element which is used for deoxidation and the strengthening of the steel. However, when Si is excessively contained, an embrittlement phase is formed in the welding heat affected zone in some cases. Therefore, it is preferable that the Si content be limited to 0.4% or less. The Si content may be 0%.

P: 0.015% or Less

P is an impurity and is segregated at the grain boundary to deteriorate the properties. Thus, the P content is preferably limited to 0.015% or less. The P content may be 0%.

S: 0.005% or Less

S is an impurity and forms sulfides such as MnS or the like to deteriorate the properties. Therefore, it is preferable that the S content be limited to 0.005% or less. The S content may be 0%.

N: 0.007% or Less

N is an element which forms nitrides such as TiN or the like and fine TiN is used for the refinement of the structure. However, when N is excessively contained, coarse nitrides are formed and the properties are deteriorated. Therefore, it is preferable that the N content be limited to 0.007% or less. The N content may be 0%.

In the steel pipe according to the embodiment, further, Cu, Ni, Cr, Mo, and V which contribute to strengthening may be contained within the following ranges as necessary. Since these chemical elements are not necessarily added in the steel sheet, all the lower limits of the chemical elements are limited to 0% and thus, are not limited.

Cu: 0.1% or More and 1.0% or Less

Cu is an element which increases the hardenability of the steel to increase the strength of the steel. In order to obtain the effect, it is preferable that the Cu content be 0.1% or more. However, when the Cu content exceeds 1.0%, weldability is reduced or cracking occurs on the surface of the steel during rolling in some cases. Accordingly, the Cu content is limited to 1.0% or less. The Cu content is more preferably 0.95% or less, and even more preferably 0.5% or less, and 0.2% or less.

Ni: 0.1% or More and 1.0% or Less

Ni is an element which increases the hardenability of the steel to increase the strength of the steel, and contributes to the improvement of low temperature toughness. In order to obtain the effects, it is preferable that the Ni content is 0.1% or more. However, when the Ni content exceeds 1.0%, there is a concern that weldability may be reduced. Therefore, the Ni content is limited to 1.0% or less. The Ni content is more preferably 0.5% or less, and more preferably 0.3% or less.

Cr: 0.1% or More and 1.0% or Less

Cr is an element which increases the hardenability of the steel to increase the strength of the steel. In order to obtain the effect, it is preferable that the Cr content is 0.1% or more. However, when the Cr content exceeds 1.0%, there is a concern that weldability may be deteriorated. Accordingly, the additional amount is limited to 1.0% or less. The Cr content is more preferably 0.5% or less.

Mo: 0.05% or More and 0.3% or Less

Mo is an element which increases the hardenability of the steel to increase the strength of the steel, and contributes to the improvement of low temperature toughness. In order to obtain the effects, it is preferable that Mo is contained 0.05% or more. However, when the Mo content exceeds 0.3%, a large number of low temperature transformation phases are formed or precipitation hardening is excessively caused to deteriorate low temperature toughness. Therefore, the upper limit of the Mo content is limited to 0.3%. The upper limit of the Mo content is more preferably 0.2%.

V: 0.01% or More and 0.1% or Less

V is an element which has the same effect as Nb but the effect is smaller than the effect of Nb. In order to obtain the effect, it is preferable that the V content be 0.01% or more. Even when the V content exceeds 0.1%, the effect is saturated and also, costs increase, and thus, the upper limit is limited to 0.1%.

In the steel pipe according to the embodiment, further, if one or two kinds or more of Ca, Mg, REM, and the like contributing to inclusion form control are selectively contained, the effect is not impaired. Further, elements other than the above elements (for example, Zr, Sn, Co, As, and the like) may be contained as a raw material to be used including additive alloy or unavoidable impurities which are eluted from a refractory lining or the like in melting within a range as long as the properties are not deteriorated. When the amounts of Cu, Ni, Cr, Mo, and V are less than the above lower limits, the elements are treated as unavoidable impurities.

The steel pipe used in the pipeline as described above is generally produced from plural pieces of molten steel. Therefore, one steel pipe and the other steel pipe which are welded to each other are produced from different molten steel in many cases. The yield strength is significantly affected by chemical components, particularly, Ceq expressed by the following Expression. Therefore, when ΔYS as the yield strength difference is decreased, decrease in a ΔCeq value which is an absolute value of the difference between Ceq values in the one steel pipe and the other steel pipe is effective. If the ΔCeq value is decreased, ΔTS is decreased. When the above-described Expression (b) or (f) is satisfied, ΔCeq is preferably 0.045 or less. ΔCeq is more preferably 0.035 or less. In addition, the one steel pipe and the other steel pipe may be produced from the same molten steel, and in this case, ΔCeq is 0.

Ceq=[C]+[Mn]/6+([Ni]+[Cu])/15+([Cr]+[Mo]+[V])/5  (d)

Here, [C], [Mn], [Ni], [Cu], [Cr], [Mo], and [V] represent the amounts, in mass %, of C, Mn, Ni, Cu, Cr, Mo, and V.

When Ni, Cu, Cr, Mo, and V are not contained, members respectively representing the element contents are 0. In this case, Expression (d) can be substituted by the following Expression (c).

Ceq=[C]+[Mn]/6  (c)

Next, a method of producing a pipeline according to an embodiment of the present invention will be described.

For example, as shown in FIG. 5A, before all of plural steel pipes used in the pipeline are joined to each other by welding, the yield strength of each steel pipe is measured. Then, one steel pipe and the other steel pipe to be welded may be selected and welded such that the above-mentioned Expression (b) is satisfied in the steel pipe showing a round type SS curve and the above-mentioned Expression (f) is satisfied in the steel pipe showing a YPE type SS curve based on the yield strength measurement result. According to the method, regardless of the components of the steel pipe and the history of production conditions, steel pipes in which ΔYS as the yield strength difference is small can be reliably welded to each other. It is possible to produce the pipeline in which the deformation properties of the steel pipes are sufficiently exhibited by welding the steel pipes selected in the above manner over the entire length.

The measurement of yield strength may be performed, for example, according to a total thickness tensile testing method defined by API Specification 5L.

In addition, when the tensile strength of all steel pipes is not easily measured, as shown in FIG. 5B, production numbers that can specify the respective steel pipes are assigned to all steel pipes used in the pipeline in order of rolling (for example, X+1, X+2, . . . , X+N, and the like in order of rolling). Then, the steel pipes produced from the same molten steel and the same hot-rolled coil and having a difference between the production numbers of 1 or more and 5 or less may be welded.

When the steel pipes are not produced from the same molten steel and the same hot-rolled coil, a large yield strength difference between each steel pipe may be generated by variation in components and production conditions such as rolling conditions and the like. In addition, when the steel pipes are produced from the same molten steel and the same hot-rolled coil, the steel pipes having a large difference between the assigned production numbers have different cooling conditions when the steel pipes are coiled around a coil and thus, a large yield strength difference between the steel pipes is generated in some cases. Therefore, it is preferable that the steel pipes produced from the same molten steel and the same hot-rolled coil and having a difference between the production numbers of 1 or more and 5 or less be welded to each other. In FIG. 5B, for convenience, the production numbers are assigned after the steel pipes are formed. However, the production members may be assigned at any stage such as rolling, cooling, or preparation of a rolling plan of a steel sheet which is the material used to form the steel pipe, as long as the rolled order is clear.

When the steel pipes to be welded to each other are determined using the above-described method, the method of producing a steel pipe used in the pipeline according to the embodiment is not particularly limited and the pipeline may be produced by a conventional method depending on property desired. However, when a steel pipe having properties suitable for practical use (for example, properties which satisfy X42 to X80 defined by API Specification 5L) is obtained as for the steel pipe used in the pipeline, round type and YPE type steel pipes can be easily produced by, for example, adopting the following production method.

Examples of a pipe-making method and a production method depending on a SS curve type will be described.

(i) Electric Resistance Welded Steel Pipe (ERW) Having Tensile Strength of 450 MPa or More and 850 MPa or Less and Showing Round Type SS Curve

A slab having chemical components in the above-described preferable ranges is heated to 1200° C. or higher and 1300° C. or lower and the heated slab is subjected to rough rolling to form a steel. The steel is subjected to finish rolling so that the rolling end temperature becomes 800° C. or higher and 900° C. or lower. After the finish rolling is completed, the steel is cooled from a temperature range of 780° C. or higher to a temperature range of 400° C. or higher and 600° C. or lower. The cooled steel is coiled in a temperature range of 400° C. or higher and 580° C. or lower to form a hot-rolled coil. After the hot-rolled coil is cooled to room temperature, an open pipe is formed by roll forming while the hot-rolled coil is uncoiled. The seam zone of the open pipe is welded by electric sewing welding and the electric resistance weld zone is subjected to seam heat treatment. Thus, it is possible to form a round type electric resistance welded steel pipe.

(ii) Case of UOE Steel Pipe Having Tensile Strength of 450 MPa or More and 850 MPa or Less and Showing Round Type SS Curve

A slab having chemical components in the above-described preferable ranges is heated to 1100° C. or higher and 1200° C. or lower and the heated slab is subjected to rough rolling to form a steel. The steel is subjected to finish rolling so that a rolling end temperature becomes 700° C. or higher and 850° C. or lower. After the finish rolling is completed, the steel is cooled from a temperature range of 700° C. or higher to a temperature range of 500° C. or lower. Then, the cooled steel is cooled to room temperature to form a steel sheet. A round type UOE steel pipe can be formed by making the steel sheet into a pipe using a known UOE method.

When a method such as (i) or (ii) is used, it is possible to stably produce a round type steel pipe having a tensile strength of 450 MPa or more and 850 MPa or lower. In the above-described production methods, the reason that the SS curve is a round type, is that strain caused by forming at cold rolling in a pipe-making state is present.

(iii) Case of YPE type electric resistance welded steel pipe having tensile strength of 450 MPa or more and 850 MPa or less

A slab having a predetermined steel composition is heated to 1200° C. or higher and 1300° C. or lower and the heated slab is subjected to rough rolling to form a steel. The steel is subjected to finish rolling so that a rolling end temperature becomes 800° C. or higher and 900° C. or lower. After the finish rolling is completed, the steel is cooled from a temperature range of 780° C. or higher to a temperature range of 400° C. or higher and 600° C. or lower. The cooled steel is coiled in a temperature range of 400° C. or higher and 580° C. or lower to form a hot-rolled coil. The hot-rolled coil is subjected to ERW forming according to a conventional method to make a pipe. After the ERW forming, a YPE type electric resistance welded steel pipe can be formed by performing heat treatment such as quenching and tempering (QT), tempering (T) or aging treatment. When QT is performed, for example, after heating to 900° C. to 980° C., water cooling and then, tempering at a temperature of 500° C. to 700° C. may be performed depending on a desired property. When only tempering is performed, the tempering may be performed at a temperature of 300° C. to 700° C.

(iv) Case of YPE Type Seamless Steel Pipe Having Tensile Strength of 450 MPa or More and 850 MPa or Lower

A bloom having a predetermined steel composition is heated to 1200° C. or higher and 1300° C. or lower, formed into a steel pipe by a so-called Mannesmann production method, and air-cooled. Then, quenching (Q) in which the steel pipe is heated to 900° C. or higher and 950° C. or lower and water-cooled and tempering (T) in which the steel pipe is heated to 500° C. or higher and 700° C. or lower are performed and air cooling is performed. Thus, it is possible to form a YPE type seamless steel pipe.

(v) Others

In addition, by coating a round type steel pipe produced by a method such as (i) or (ii) with thermosetting resin, a YPE type steel pipe can be formed. The coating with thermosetting resin can be performed by, for example, heating the steel pipe to a temperature range of 200° C. to 250° C. with a ring-shaped induction heater or the like and spraying thermosetting resin such as epoxy resin or the like in the temperature range with a spray or the like.

Further, by heating a round type steel pipe produced by a method such as (i) or (ii) to a temperature range of about 200° C. to 250° C. and retaining the steel pipe in the temperature range for 10 minutes or longer to cause strain aging, a YPE type steel pipe can be formed. This is because an interstitial solid solution element such as C or N is fixed to the dislocation in the steel as time elapses.

Since the coating with the thermal process type resin and the aging are treatments for heating the steel pipe to the same temperature range, the coating and the aging treatment have nearly the same level of influence on the mechanical properties of the steel pipe.

When methods such as (iii) to (v) are used, it is possible to stably produce a YPE type steel pipe having a tensile strength of 450 MPa or more and 850 MPa or less.

In addition, the electric resistance welded steel pipe (ERW steel pipe) can be produced with high productivity at low cost. Further, the seamless steel pipe has properties in which a steel pipe having high t/D is easily produced.

Examples

Next, the present invention will be further described using Examples. The conditions in the examples are simply an example of conditions employed to confirm the feasibility and effect of the present invention, and the present invention is not limited to the example of conditions. The present invention can employ a variety of conditions without departing from the gist of the present invention as long as the objective of the present invention can be achieved.

In order to simulate a stress state when a steel pipe is coiled around or uncoiled from the drum, the buckling properties of a girth-welded steel pipe were evaluated using a testing apparatus which imparts a bending moment on the pipe end so as to be arranged along a bed having a radius of 3750 mm. The outline of a testing apparatus 10 used in Examples is shown in FIG. 4.

In the testing apparatus 10, an unbending bed 11 and a bending bed 12 are vertically disposed. The lower surface of the unbending bed 11 is a curved surface which is convex downward and the upper surface of the bending bed 12 is a curved surface which is convex upward. As shown in the drawing, out of the two steel pipes 2 (steel pipes A and B) whose ends are joined by girth welding in the weld zone 3, an end of the steel pipe A opposite to the weld zone 3 is interposed between the lower surface of the unbending bed 11 and the upper surface of the bending bed 12 to be fixed. Then, a bending load 13 is applied to an end of the steel pipe B opposite to the weld zone 3. In this case, the steel pipes A and B are curved along the upper surface of the bending bed 12 by applying the bending load 13 downwardly. Accordingly, a load of the same condition as in the case where the steel pipes are wound around the drum is applied to the steel pipes A and B. On the other hand, the steel pipes A and B are curved along the lower surface of the unbending bed 11 by applying the bending load 13 upwardly. Accordingly, the curved steel pipes A and B are stretched linearly, that is, a load of the same condition as in unbending is applied.

In order to demonstrate the index obtained from HA, the two steel pipes A and B joined by girth-welding were subjected to a bending test using the testing apparatus 10 shown in FIG. 4. As the steel pipes A and B, as shown in Tables 2 to 28, steel sheets having steel compositions shown in Table 1 and produced under the conditions of Tables 2 to 10 were made into steel pipes having outer diameters and thicknesses shown in Tables 11 to 19, and the steel pipes which were subjected to heat treatment, aging treatment, or coating with thermosetting resin were used as necessary. The bed diameter was set as shown in Tables 20 to 28. The ΔYS of the steel pipes A and B was as shown in Tables 20 to 28.

Blank spaces in Table 1 indicate that the content was a measurement limit value or less. In the aging treatment in Table 15, the steel pipe was heated to 200° C. and retained in the temperature range for 10 minutes. In the tempering in Table 15, the steel pipe was heated to 600° C. In QT in Tables 13 and 14, quenching in which the steel pipe is water-cooled after heating to 930° C., and tempering in which the steel pipe is heated to 650° C. were performed. The coating with thermosetting resin was performed such that the steel pipe was heated to a temperature range of 200° C. to 250° C. with a ring-shaped induction heater or the like and epoxy resin was sprayed with a spray or the like in the temperature range. The tensile test of the steel sheet and the steel pipe was performed according to a total thickness tensile testing method defined by API Specification 5L.

In consideration of additional bending and unbending in the laying work, or bending in grounding on the seabed, in the testing apparatus 10 shown in FIG. 4, an operation of applying the bending load 13 downwardly to bend the steel pipes A and B, and an operation of applying the bending load 13 upwardly to unbend the steel pipes A and B were alternately repeated three cycles. As a result, when ΔYS is −1.75×YR+230 or less, in the case of the round type and when ΔYS is ×0.69×YR+125 or less in the case of the YPE type, as in the test numbers 1 to 26, 46 to 65, 82 to 91, 103 to 105, 106 to 108, 111 to 115, 120, 121, 123 to 126, and 128 to 130, it was found that local buckling did not occur in bending and the joint was not fractured during three cycles of bending and unbending.

On the other hand, when ΔYS exceeds −1.75×YR+230 in the case of the round type (examples in which the type of the SS curve is round in Tables), and when ΔYS exceeds −0.69×YR+125 in the case of the YPE type (examples in which the type of the SS curve is YPE), local buckling was observed at the inner arc edge on the compressive side in the third unbending, and fracture occurred from the vicinity of the weld zone at the outer arc edge. The fractured place is a portion in which local buckling occurs at the time when the bending load is applied. It can be considered that strain is concentrated at the time of bending and unbending and the strain is accumulated to cause fracture.

Test results are suggested that the welded joint which satisfies the conditions of Expressions (b) and (f) is effective in an environment of usage in which the welded joint is subjected to coiling and uncoiling.

In addition, as seen from the test numbers 128 to 130, ΔYS satisfied Expression (b) in the steel pipe produced from the same molten steel and having the difference between the production numbers be within 5 and the joint was not fractured during three cycles of bending and unbending.

[Table 1]

[Table 2]

[Table 3]

[Table 4]

[Table 5]

[Table 6]

[Table 7]

[Table 8]

[Table 9]

[Table 10]

[Table 11]

[Table 12]

[Table 13]

[Table 14]

[Table 15]

[Table 16]

[Table 17]

[Table 18]

[Table 19]

[Table 20]

[Table 21]

[Table 22]

[Table 23]

[Table 24]

[Table 25]

[Table 26]

[Table 27]

[Table 28]

INDUSTRIAL APPLICABILITY

According to the present invention, it is possible to provide the pipeline in which the deformation properties of the steel pipe are sufficiently exhibited and thus, the present invention very remarkably contributes to the industry.

BRIEF DESCRIPTION OF THE REFERENCE SYMBOLS

-   -   1: PIPELINE     -   2, A, B: STEEL PIPE     -   3: WELD ZONE     -   4: DRUM     -   5: HEAT AFFECTED ZONE (HAZ)     -   10: TESTING APPARATUS     -   11: UNBENDING BED     -   12: BENDING BED     -   13: BENDING LOAD

TABLE 1 Steel Component composition (mass %) Ceq type C Si Mn P S Nb Al Ti N Mo Cu Ni Cr V (%) A1 0.080 0.19 1.35 0.009 0.001 0.080 0.02 0.006 0.0035 0.305 A2 0.083 0.19 1.35 0.009 0.001 0.080 0.02 0.006 0.0038 0.308 A3 0.090 0.19 1.35 0.009 0.001 0.080 0.02 0.006 0.0035 0.315 A4 0.098 0.19 1.35 0.009 0.001 0.080 0.02 0.007 0.0039 0.323 A5 0.100 0.20 1.35 0.010 0.002 0.015 0.02 0.009 0.0042 0.325 B1 0.045 0.20 1.35 0.010 0.001 0.025 0.02 0.011 0.0020 0.06 0.19 0.320 B2 0.050 0.23 1.40 0.010 0.001 0.025 0.02 0.012 0.0030 0.06 0.20 0.335 B3 0.055 0.25 1.45 0.011 0.003 0.025 0.02 0.013 0.0020 0.07 0.18 0.347 C1 0.055 005 1.59 0.012 0.003 0012 0.04 0.012 0.0045 0.13 0.13 0.05 0.03 0.353 C2 0.058 0.06 1.60 0.011 0.002 0.008 0.03 0.010 0.0038 0.13 0.14 0.05 0.03 0.359 C3 0.066 0.09 1.63 0.009 0.002 0.009 0.03 0.013 0.0041 0.13 0.16 0.08 0.04 0.381 C4 0.070 0.10 1.67 0.013 0.003 0.013 0.03 0.011 0.0036 0.18 0.18 0.10 0.03 0.398 D1 0.080 0.25 1.26 0.015 0.003 0.040 0.05 0.013 0.0051 0.05 0.300 D2 0.090 0.28 1.31 0.013 0.002 0.050 0.04 0.012 0.0049 0.05 0.318 D3 0.100 0.28 1.31 0.013 0.003 0.050 0.04 0.012 0.0048 0.06 0.330 E1 0.040 0.30 1.37 0.010 0.001 0.013 0.02 0.010 0.0030 0.13 0.21 0.41 0.390 E2 0.050 0.35 1.40 0.010 0.001 0.013 0.02 0.012 0.0060 0.13 0.22 0.43 0.410 E3 0.055 0.36 1.44 0.011 0.003 0.015 0.02 0.013 0.0070 0.15 0.25 0.44 0.430

TABLE 2 Hot rolling condition Steel Heating Finish rolling Rolling end Cooling start Coiling Steel sheet Test pipe Steel temperature reduction temperature temperature temperature YS TS YR number A or B type [° C.] [%] [° C.] [° C.] [° C.] [MPa] [MPa] [%] 1 A A1 1230 80 860 820 490 379 527 72 B A4 1230 80 860 820 560 401 531 76 2 A A1 1230 80 860 820 530 343 504 68 B A4 1230 80 860 810 510 406 572 71 3 A A4 1230 80 860 820 530 407 528 77 B A4 1230 80 860 820 500 420 538 78 4 A A1 1230 80 860 820 530 354 479 74 B A4 1230 80 860 820 530 411 534 77 5 A A3 1230 80 860 820 560 376 530 71 B A1 1230 80 860 810 510 350 538 65 6 A A1 1230 80 860 820 530 345 454 76 B A4 1230 80 860 820 570 394 512 77 7 A A1 1230 80 860 820 530 345 480 72 B A3 1230 80 860 820 500 398 530 75 8 A A1 1230 80 860 810 510 355 495 72 B A3 1230 80 860 820 530 385 520 74 9 A A2 1230 80 860 820 560 362 489 74 B A4 1230 80 860 820 570 397 522 76 10 A A5 1230 80 860 820 450 467 577 81 B A4 1230 80 860 800 420 476 580 82 11 A A2 1230 80 860 810 510 382 512 75 B A1 1230 80 860 820 500 372 523 71 12 A B2 1230 80 860 820 500 412 532 77 B B3 1230 80 860 800 470 436 590 74 13 A B1 1230 80 860 820 500 367 510 72 B B2 1230 80 860 820 530 386 529 73 14 A B2 1230 80 860 820 530 395 541 73 B B1 1230 80 860 810 550 340 485 70 15 A B1 1230 80 860 800 470 409 541 78 B B1 1230 80 860 820 500 374 505 74 16 A C2 1230 80 860 810 550 375 510 74 B C2 1230 80 860 810 510 391 532 73 17 A C4 1230 80 860 820 530 433 528 82 B C2 1230 80 860 820 450 434 536 81 18 A C1 1230 80 860 810 550 363 472 77 B C4 1230 80 860 800 470 446 525 85 19 A C1 1230 80 860 820 500 394 512 77 B C2 1230 80 860 810 540 387 530 73 20 A C1 1230 80 860 810 550 353 512 69 B C1 1230 80 860 810 510 385 528 73 21 A C2 1230 80 860 820 570 371 501 74 B C2 1230 80 860 820 530 390 522 75 22 A C3 1230 80 860 810 550 400 515 78 B C3 1230 80 860 810 540 398 528 78 23 A C2 1230 80 860 820 570 371 515 72 B C3 1230 80 860 810 510 410 540 78 24 A C4 1230 80 860 810 510 433 535 81 B C1 1230 80 860 820 530 365 545 67 25 A C1 1230 80 860 810 550 349 529 68 B C1 1230 80 860 820 530 367 532 69 26 A C2 1230 80 860 820 500 401 540 74 B C2 1230 80 860 810 480 413 525 79

TABLE 3 Hot rolling condition Steel Heating Finish rolling Rolling end Cooling start Coiling Steel sheet Test pipe Steel temperature reduction temperature temperature temperature YS TS YR number A or B type [° C.] [%] [° C.] [° C.] [° C.] [MPa] [MPa] [%] 27 A A2 1230 80 860 820 530 365 504 72 B A4 1230 80 860 820 490 430 587 73 28 A A3 1230 80 860 810 510 398 485 82 B A5 1230 80 860 800 420 474 600 79 29 A A2 1230 80 860 820 530 358 512 70 B A4 1230 80 860 820 450 441 580 76 30 A A5 1230 80 860 820 570 437 540 81 B A3 1230 80 860 810 510 402 479 84 31 A A2 1230 80 860 820 570 341 542 63 B A5 1230 80 860 820 490 445 571 78 32 A A3 1230 80 860 820 530 385 514 75 B A4 1230 80 860 800 470 430 600 72 33 A A2 1230 80 860 820 560 365 474 77 B A4 1230 80 860 810 510 415 552 75 34 A A2 1230 80 860 810 510 389 474 82 B A4 1230 80 860 800 470 444 562 79 35 A A2 1230 80 860 820 530 358 512 70 B A5 1230 80 860 800 470 466 568 82 36 A A2 1230 80 860 820 530 365 482 76 B A4 1230 80 860 820 500 426 554 77 37 A B1 1230 80 860 820 530 388 500 74 B B2 1230 80 860 800 470 421 587 72 38 A B1 1230 80 860 820 530 384 505 72 B B1 1230 80 860 820 450 434 595 73 39 A B1 1230 80 860 820 530 365 485 75 B B3 1230 80 860 820 450 451 593 76 40 A C2 1230 80 860 820 570 371 505 73 B C3 1230 80 860 800 470 425 582 73 41 A C1 1230 80 860 810 540 369 498 74 B C3 1230 80 860 820 450 450 570 79 42 A C2 1230 80 860 810 540 385 493 78 B C1 1230 80 860 810 480 398 555 72 43 A C1 1230 80 860 810 550 364 480 76 B C3 1230 80 860 810 540 400 538 74 44 A C2 1230 80 860 800 470 424 550 77 B C1 1230 80 860 820 570 354 485 73 45 A C3 1230 80 860 820 570 395 502 79 B C2 1230 80 860 810 480 416 568 73

TABLE 4 Hot rolling condition Steel Heating Finish rolling Rolling end Cooling start Coiling Steel sheet Test pipe Steel temperature reduction temperature temperature temperature YS TS YR number A or B type [° C.] [%] [° C.] [° C.] [° C.] [MPa] [MPa] [%] 48 A A4 1230 80 860 820 560 395 525 75 B A3 1230 80 860 800 480 421 560 75 47 A A1 1230 80 860 810 510 365 500 73 B A2 1230 80 860 810 510 371 515 72 48 A A4 1230 80 860 820 530 400 540 74 B A4 1230 80 860 800 470 420 568 74 49 A A4 1230 80 860 820 560 393 531 74 B A4 1230 80 860 810 510 410 547 75 50 A A4 1230 80 860 820 500 400 549 73 B A4 1230 80 860 820 500 419 564 74 51 A A4 1230 80 860 820 560 411 542 76 B A4 1230 80 860 810 510 426 558 76 52 A A1 1230 80 860 810 510 351 495 71 B A4 1230 80 860 810 510 418 550 76 53 A A4 1230 80 860 810 510 401 549 73 B A5 1230 80 860 800 420 452 603 75 54 A A4 1230 80 860 800 470 441 612 72 B A4 1230 80 860 820 570 398 522 76 55 A B1 1230 80 860 820 500 367 500 73 B B1 1230 80 860 800 470 414 553 75 56 A B1 1230 80 860 820 500 361 516 70 B B2 1230 80 860 820 530 369 520 71 57 A B1 1230 80 860 820 530 384 497 77 B B2 1230 80 860 800 470 435 587 74 58 A C3 1230 80 860 810 510 408 545 75 B C3 1230 80 860 800 470 432 580 74 59 A C2 1230 80 860 810 510 383 540 71 B C1 1230 80 860 820 530 375 535 70 60 A C1 1230 80 860 810 550 346 509 68 B C2 1230 80 860 800 470 416 555 75 61 A C2 1230 80 860 810 480 418 566 74 B C3 1230 80 860 820 450 445 578 77 62 A C1 1230 80 860 810 510 388 524 74 B C2 1230 80 860 810 550 380 506 75 63 A C3 1230 80 860 810 540 406 534 76 B C3 1230 80 860 820 450 444 576 77 64 A C2 1230 80 860 820 570 364 512 71 B C2 1230 80 860 810 480 416 578 72 65 A C3 1230 80 860 820 450 448 578 78 B C1 1230 80 860 810 510 382 528 72

TABLE 5 Hot rolling condition Steel Heating Finish rolling Rolling end Cooling start Coiling Steel sheet Test pipe Steel temperature reduction temperature temperature temperature YS TS YR number A or B type [° C.] [%] [° C.] [° C.] [° C.] [MPa] [MPa] [%] 66 A C2 1230 80 860 820 570 378 513 74 B C3 1230 80 860 800 470 423 580 73 67 A C3 1230 80 860 810 510 416 540 77 B C4 1230 80 860 800 470 458 603 76 68 A C3 1230 80 860 810 550 413 510 81 B C3 1230 80 860 820 450 471 574 82 69 A A2 1230 80 860 820 530 365 499 73 B A4 1230 60 860 810 510 412 554 74 70 A A4 1230 80 860 820 570 390 520 75 B A5 1230 80 860 820 490 440 562 78 71 A A2 1230 80 860 810 510 383 517 74 B A4 1230 80 860 820 450 434 586 74 72 A A4 1230 80 860 820 530 397 544 73 B A1 1230 80 860 810 510 342 495 69 73 A B1 1230 80 860 820 530 350 500 70 B B2 1230 80 860 800 470 435 573 76 74 A B1 1230 80 860 820 500 384 511 75 B B3 1230 80 860 820 450 450 584 77 75 A B2 1230 80 860 820 530 394 519 76 B B3 1230 80 860 820 450 465 591 79 76 A C3 1230 80 860 810 540 408 525 78 B C3 1230 80 860 800 470 436 581 75 77 A C3 1230 80 860 820 570 399 505 79 B C3 1230 80 860 820 450 464 580 80 78 A C2 1230 80 860 820 570 375 515 73 B C2 1230 80 860 800 470 432 548 79 79 A C1 1230 80 860 810 550 345 470 73 B C2 1230 80 860 810 480 417 560 74 80 A C2 1230 80 860 820 570 361 494 73 B C3 1230 80 860 800 470 418 589 71 81 A C3 1230 80 860 810 540 399 532 75 B C3 1230 80 860 800 470 425 584 73

TABLE 6 Hot rolling condition Steel Heating Finish rolling Rolling end Cooling start Coiling Steel sheet Test pipe Steel temperature reduction temperature temperature temperature YS TS YR number A or B type [° C.] [%] [° C.] [° C.] [° C.] [MPa] [MPa] [%] 82 A A4 1230 80 860 820 570 390 524 74 B A4 1230 80 860 820 570 407 527 77 83 A A3 1230 80 860 820 500 397 530 75 B A5 1230 80 860 820 490 421 571 74 84 A A1 1230 80 860 820 490 388 530 73 B A5 1230 80 860 820 490 445 574 78 85 A A4 1230 80 860 820 490 435 581 75 B A4 1230 80 860 820 490 439 586 75 86 A B3 1230 80 860 820 500 427 570 75 B B3 1230 80 860 800 470 448 586 76 87 A B1 1230 80 860 820 530 355 489 73 B B2 1230 80 860 820 500 405 535 76 88 A C1 1230 80 860 810 480 402 560 72 B C2 1230 80 860 800 470 425 557 76 89 A C2 1230 80 860 810 540 355 490 72 B C1 1230 80 860 810 550 367 481 76 90 A C2 1230 80 860 800 470 420 548 77 B C3 1230 80 860 800 470 415 580 72 91 A C3 1230 80 860 820 450 436 570 76 B C2 1230 80 860 820 500 418 541 77 92 A A2 1230 80 860 820 530 367 505 73 B A3 1230 80 860 810 450 468 605 77 93 A A2 1230 80 860 820 560 368 476 77 B A4 1230 80 860 820 530 415 540 77 94 A A1 1230 80 860 820 530 333 450 74 B A4 1230 80 860 820 570 398 521 76 95 A A4 1230 80 860 820 570 393 510 77 B A5 1230 80 860 800 470 452 565 80 96 A A4 1230 80 860 820 500 420 541 75 B A2 1230 80 860 820 530 374 499 75 97 A B2 1230 80 860 820 530 385 544 71 B B2 1230 80 860 800 470 438 581 75 98 A B1 1230 80 860 820 500 374 510 73 B B2 1230 80 860 800 470 450 575 78 99 A C3 1230 80 860 810 510 411 549 75 B C2 1230 80 860 810 480 422 571 74 100 A C4 1230 80 860 810 510 420 534 79 B C4 1230 80 860 800 470 458 599 76 101 A C2 1230 80 860 810 540 385 530 73 B C3 1230 80 860 800 470 430 595 72 102 A C2 1230 80 860 820 570 375 494 76 B C4 1230 80 860 820 440 482 635 76 103 A A1 1230 80 860 820 500 398 528 75 B A5 1230 80 860 820 490 450 575 78 104 A B1 1230 80 860 820 530 350 495 71 B B2 1230 80 860 820 510 399 534 75 105 A C2 1230 80 860 800 480 410 545 75 B C3 1230 80 860 800 470 418 580 72

TABLE 7 Hot rolling condition Steel Heating Finish rolling Rolling end Cooling start Coiling Steel sheet Test pipe Steel temperature reduction temperature temperature temperature YS TS YR number A or B type [° C.] [%] [° C.] [° C.] [° C.] [MPa] [MPa] [%] 106 A C1 1230 80 860 810 550 338 472 72 B C1 1230 80 860 810 540 364 499 73 107 A C1 1230 80 860 820 570 341 487 70 B C2 1230 80 860 810 540 383 532 72 108 A C2 1230 80 860 810 550 385 510 75 B C3 1230 80 860 810 540 410 525 78 109 A C1 1230 80 860 810 550 345 462 75 B C2 1230 80 860 810 510 388 533 73 110 A C1 1230 80 860 810 580 340 454 75 B C3 1230 80 860 820 450 446 571 78 111 A C4 1230 80 860 820 440 467 640 73 B C4 1230 80 860 820 430 500 675 74 112 A C4 1230 80 860 820 440 480 624 77 B C4 1230 80 860 820 440 471 628 75 113 A C4 1230 80 860 820 440 466 623 75 B C4 1230 80 860 820 430 509 668 76 114 A C4 1230 80 860 820 430 397 567 70 B C1 1230 80 860 810 480 402 566 71 115 A C4 1230 80 860 820 440 460 635 72 B C4 1230 80 860 800 470 475 610 78 116 A C3 1230 80 860 800 470 430 582 74 B C4 1230 80 860 820 440 485 649 75 117 A C4 1230 80 860 800 470 467 600 78 B C4 1230 80 860 820 430 500 657 76 118 A C4 1230 80 860 820 440 463 628 74 B C4 1230 80 860 820 420 518 700 74 119 A C4 1230 80 860 820 440 480 631 76 B C4 1230 80 860 820 420 547 715 77

TABLE 8 Hot rolling condition Steel Heating Test pipe Steel temperature number A or B type [° C.] Production method after heating 120 A D1 1260 Air cooling after B D1 1260 hot rolling by Mannesmann 121 A D2 1260 production method B D3 1260 122 A D1 1260 B D3 1260

TABLE 9 Hot rolling condition Steel Heating Finish rolling Rolling end Cooling start Coiling Steel sheet Test pipe Steel temperature reduction temperature temperature temperature YS TS YR number A or B type [° C.] [%] [° C.] [° C.] [° C.] [MPa] [MPa] [%] 123 A E1 1150 80 830 800 410 469 565 83 B E1 1150 80 840 800 360 487 580 84 124 A E2 1150 80 770 750 350 494 633 78 B E3 1150 80 770 760 320 541 652 83 125 A E3 1150 80 750 740 270 539 682 79 B E3 1150 80 740 730 180 528 675 78 126 A E1 1150 80 800 770 385 456 570 80 B E2 1150 80 790 760 410 494 610 81 127 A E1 1150 80 820 780 400 466 568 82 B E3 1150 80 760 740 210 547 692 79

TABLE 10 Hot rolling condition Steel Heating Finish rolling Rolling end Cooling start Coiling Steel sheet Test pipe Steel temperature reduction temperature temperature temperature YS TS YR number A or B type [° C.] [%] [° C.] [° C.] [° C.] [MPa] [MPa] [%] 128 A A4 1230 80 860 820 570 394 512 77 B 1230 80 860 820 570 397 522 76 129 A B2 1230 80 860 820 530 386 529 77 B 1230 80 860 820 530 395 541 73 130 A C2 1230 80 860 820 570 371 501 74 B 1230 80 860 820 570 371 515 72

TABLE 11 Steel pipe Pipe- Outer Coating with Type of Test making diameter Thickness Heat thermosetting YS TS YR SS number method [mm] [mm] treatment resin [MPa] [MPa] [%] curve 1 ERW 193.7 9.53 None None 470 553 85 Round 500 568 88 Round 2 ERW None None 460 541 85 Round 530 596 89 Round 3 ERW None None 500 556 90 Round 500 568 88 Round 4 ERW None None 455 506 90 Round 520 559 93 Round 5 ERW None None 470 553 85 Round 500 568 88 Round 6 ERW None None 460 489 94 Round 510 537 95 Round 7 ERW None None 490 505 97 Round 550 561 98 Round 8 ERW 10.5 None None 450 511 88 Round 510 554 92 Round 9 ERW None None 450 511 88 Round 490 551 89 Round 10 ERW None None 560 602 93 Round 590 615 96 Round 11 ERW None None 470 540 87 Round 520 553 94 Round 12 ERW 304.8 12 None None 470 553 85 Round 550 625 88 Round 13 ERW None None 460 541 85 Round 470 553 85 Round 14 ERW None None 510 567 90 Round 460 517 89 Round 15 ERW None None 530 564 94 Round 470 534 88 Round 16 ERW 323.9 17.5 None None 470 534 88 Round 500 556 90 Round 17 ERW None None 520 553 94 Round 540 557 97 Round 18 ERW None None 480 505 95 Round 540 557 97 Round 19 ERW None None 470 534 88 Round 500 556 90 Round 20 ERW None None 470 534 88 Round 500 556 90 Round 21 ERW None None 470 534 88 Round 500 556 90 Round 22 ERW 508 22 None None 460 548 84 Round 480 552 87 Round 23 ERW None None 460 548 84 Round 520 578 90 Round 24 ERW None None 530 564 94 Round 470 566 83 Round 25 ERW None None 450 549 82 Round 470 566 83 Round 26 ERW None None 520 565 92 Round 530 564 94 Round

TABLE 12 Steel pipe Pipe- Outer Coating with Type of Test making diameter Thickness Heat thermosetting YS TS YR SS number method [mm] [mm] treatment resin [MPa] [MPa] [%] curve 27 ERW 193.7 9.53 None None 450 536 84 Round 540 614 88 Round 28 ERW None None 480 505 95 Round 550 625 88 Round 29 ERW None None 450 536 84 Round 540 614 88 Round 30 ERW None None 550 573 96 Round 480 500 96 Round 31 ERW None None 450 563 80 Round 550 598 92 Round 32 ERW None None 450 536 84 Round 540 621 87 Round 33 ERW 10.5 None None 470 500 94 Round 540 587 92 Round 34 ERW None None 480 500 96 Round 550 585 94 Round 35 ERW None None 450 542 83 Round 560 596 94 Round 36 ERW None None 450 500 90 Round 530 570 93 Round 37 ERW 304.8 12 None None 460 535 86 Round 550 618 89 Round 38 ERW None None 470 528 89 Round 550 618 89 Round 39 ERW None None 480 522 92 Round 550 618 89 Round 40 ERW 323.9 17.5 None None 470 534 88 Round 550 611 90 Round 41 ERW None None 485 533 91 Round 570 600 95 Round 42 ERW None None 490 510 96 Round 555 584 95 Round 43 ERW 508 22 None None 455 506 90 Round 530 570 93 Round 44 ERW None None 540 568 95 Round 465 517 90 Round 45 ERW None None 500 532 94 Round 570 600 95 Round

TABLE 13 Steel pipe Pipe- Outer Coating with Type of Test making diameter Thickness Heat thermosetting YS TS YR SS number method [mm] [mm] treatment resin [MPa] [MPa] [%] curve 46 ERW 193.7 9.53 QT None 465 554 84 YPE 505 587 86 YPE 47 ERW QT None 455 529 86 YPE 465 541 86 YPE 48 ERW QT None 480 558 86 YPE 520 591 88 YPE 49 ERW QT None 490 563 87 YPE 520 578 90 YPE 50 ERW QT None 540 587 92 YPE 525 590 89 YPE 51 ERW 10.5 QT None 470 566 83 YPE 520 591 88 YPE 52 ERW QT None 450 529 85 YPE 513 576 89 YPE 53 ERW QT None 500 581 86 YPE 560 622 90 YPE 54 ERW QT None 550 640 86 YPE 488 555 88 YPE 55 ERW 304.8 12 QT None 448 533 84 YPE 512 582 88 YPE 56 ERW QT None 460 541 85 YPE 470 547 86 YPE 57 ERW QT None 498 535 93 YPE 547 615 89 YPE 58 ERW 323.9 17.5 QT None 504 573 88 YPE 547 615 89 YPE 59 ERW QT None 465 567 82 YPE 465 567 82 YPE 60 ERW QT None 455 542 84 YPE 520 578 90 YPE 61 ERW QT None 545 606 90 YPE 550 598 92 YPE 62 ERW 508 22 QT None 465 547 85 YPE 470 540 87 YPE 63 ERW QT None 490 557 88 YPE 540 600 90 YPE 64 ERW QT None 467 531 88 YPE 530 609 87 YPE 65 ERW QT None 513 597 86 YPE 470 566 83 YPE

TABLE 14 Steel pipe Pipe- Outer Coating with Type of Test making diameter Thickness Heat thermosetting YS TS YR SS number method [mm] [mm] treatment resin [MPa] [MPa] [%] curve 66 ERW 193.7 9.53 QT None 460 541 85 YPE 530 616 86 YPE 67 ERW QT None 490 557 88 YPE 555 631 88 YPE 68 ERW QT None 500 538 93 YPE 565 595 95 YPE 69 ERW QT None 430 524 82 YPE 503 592 85 YPE 70 ERW 10.5 QT None 470 547 86 YPE 540 600 90 YPE 71 ERW QT None 490 544 90 YPE 562 611 92 YPE 72 ERW QT None 520 571 91 YPE 452 526 86 YPE 73 ERW 304.8 12 QT None 456 530 86 YPE 535 601 89 YPE 74 ERW QT None 472 536 88 YPE 542 609 89 YPE 75 ERW QT None 500 543 92 YPE 580 617 94 YPE 76 ERW 323.9 17.5 QT None 482 548 88 YPE 550 611 90 YPE 77 ERW QT None 502 534 94 YPE 572 602 95 YPE 78 ERW QT None 475 540 88 YPE 546 575 95 YPE 79 ERW 508 22 QT None 448 498 90 YPE 526 584 90 YPE 80 ERW QT None 462 519 89 YPE 546 620 88 YPE 81 ERW QT None 510 567 90 YPE 584 615 95 YPE

TABLE 15 Steel pipe Pipe- Outer Coating with Type of Test making diameter Thickness Heat thermosetting YS TS YR SS number method [mm] [mm] treatment resin [MPa] [MPa] [%] curve 82 ERW 193.7 9.53 Aging None 488 555 88 YPE treatment 490 557 88 YPE 83 ERW Aging None 505 555 91 YPE treatment 560 596 94 YPE 84 ERW 10.5 Aging None 530 558 95 YPE treatment 582 606 96 YPE 85 ERW Aging None 542 609 89 YPE treatment 555 617 90 YPE 86 ERW 304.8 12 Tempering None 536 602 89 YPE 586 617 95 YPE 87 ERW Tempering None 472 513 92 YPE 527 561 94 YPE 88 ERW 323.9 17.5 Aging None 568 592 96 YPE treatment 546 581 94 YPE 89 ERW Aging None 460 517 89 YPE treatment 465 511 91 YPE 90 ERW 508 22 Aging None 560 571 98 YPE treatment 578 602 96 YPE 91 ERW Aging None 513 597 86 YPE treatment 470 566 83 YPE 92 ERW 193.7 9.53 Aging None 489 537 91 YPE treatment 570 640 89 YPE 93 ERW Aging None 490 505 97 YPE treatment 560 571 98 YPE 94 ERW 10.5 Aging None 460 484 95 YPE treatment 525 553 95 YPE 95 ERW Aging None 506 538 94 YPE treatment 589 601 98 YPE 96 ERW Aging None 520 571 91 YPE treatment 452 526 86 YPE 97 ERW 304.8 12 Aging None 514 578 89 YPE treatment 584 615 95 YPE 98 ERW Aging None 499 542 92 YPE treatment 590 608 97 YPE 99 ERW 323.9 17.5 Aging None 503 572 88 YPE treatment 572 602 95 YPE 100 ERW Aging None 536 570 94 YPE treatment 600 632 95 YPE 101 ERW 508 22 Tempering None 521 566 92 YPE 589 627 94 YPE 102 ERW Tempering None 508 524 97 YPE 584 664 88 YPE 103 ERW 193.7 10.5 None Existing 520 550 95 YPE 575 600 96 YPE 104 ERW 304.8 12 None Existing 470 515 91 YPE 520 555 94 YPE 105 ERW 508 22 None Existing 551 568 97 YPE 570 605 94 YPE

TABLE 16 Steel pipe Pipe- Outer Coating with Type of Test making diameter Thickness Heat thermosetting YS TS YR SS number method [mm] [mm] treatment resin [MPa] [MPa] [%] curve 106 ERW 508 22 None None 420 500 84 Round 456 524 87 Round 107 ERW None None 440 512 86 Round 505 561 90 Round 108 ERW None None 480 539 89 Round 510 554 92 Round 109 ERW None None 460 489 94 Round 530 564 94 Round 110 ERW None None 462 486 95 Round 540 600 90 Round 111 ERW 323.9 17.5 None None 590 670 88 Round 640 711 90 Round 112 ERW None None 600 652 92 Round 620 660 94 Round 113 ERW 508 22 None None 570 648 88 Round 645 694 93 Round 114 ERW None None 525 597 88 Round 530 589 90 Round 115 ERW None None 625 665 94 Round 564 641 88 Round 116 ERW 323.9 17.5 None None 565 614 92 Round 640 681 94 Round 117 ERW None None 572 636 90 Round 652 686 95 Round 118 ERW 508 22 None None 600 652 92 Round 680 723 94 Round 119 ERW None None 612 658 93 Round 686 738 93 Round

TABLE 17 Steel pipe Pipe- Outer Coating with Type of Test making diameter Thickness Heat thermosetting YS TS YR SS number method [mm] [mm] treatment resin [MPa] [MPa] [%] curve 120 SML 304.8 12 930° CQ None 515 602 86 YPE 650° CT 520 607 86 YPE 121 SML 930° CQ None 551 636 87 YPE 580° CT 598 698 86 YPE 122 SML 930° CQ None 522 606 86 YPE 650° CT 593 676 88 YPE

TABLE 18 Steel pipe Pipe- Outer Coating with Type of Test making diameter Thickness Heat thermosetting YS TS YR SS number method [mm] [mm] treatment resin [MPa] [MPa] [%] curve 123 UOE 508 22 None None 507 582 87 Round 532 602 88 Round 124 UOE None None 587 647 91 Round 597 672 89 Round 125 UOE None None 640 700 91 Round 634 695 91 Round 126 UOE None None 523 593 88 Round 556 631 88 Round 127 UOE None None 516 591 87 Round 627 707 89 Round

TABLE 19 Steel pipe Pipe- Outer Coating with Type of Test making diameter Thickness Heat thermosetting YS TS YR SS number method [mm] [mm] treatment resin [MPa] [MPa] [%] curve 128 ERW 193.7 9.53 None None 510 537 95 Round 482 550 88 Round 129 ERW 304.8 12 None None 470 553 85 Round 510 567 90 Round 130 ERW 508 22 None None 469 534 88 Round 455 548 83 Round

TABLE 20 Bed Right side of Test diameter Expression ΔYS Test number [mm] (2) [MPa] result Remarks 1 7500 81 30 Not Example fractured 2 7500 81 70 Not fractured 3 7500 73 0 Not fractured 4 7500 73 65 Not fractured 5 7500 81 30 Not fractured 6 7500 66 50 Not fractured 7 7500 60 60 Not fractured 8 7500 76 60 Not fractured 9 7500 76 40 Not fractured 10 7500 67 30 Not fractured 11 9000 78 50 Not fractured 12 10000 81 80 Not fractured 13 10000 81 10 Not fractured 14 10000 74 50 Not fractured 15 10000 76 60 Not fractured 16 15000 76 30 Not fractured 17 15000 66 20 Not fractured 18 15000 64 60 Not fractured 19 15000 76 30 Not fractured 20 15000 76 30 Not fractured 21 15000 76 30 Not fractured 22 15000 83 20 Not fractured 23 15000 83 60 Not fractured 24 15000 85 60 Not fractured 25 15000 87 20 Not fractured 26 15000 69 10 Not fractured

TABLE 21 Bed Right side of Test diameter Expression ΔYS Test number [mm] (2) [MPa] result Remarks 27 7500 83 90 fractured Comparative 28 7500 64 70 fractured example 29 7500 83 90 fractured 30 7500 62 70 fractured 31 7500 90 100 fractured 32 7500 83 90 fractured 33 7500 66 70 fractured 34 7500 62 70 fractured 35 7500 85 110 fractured 36 7500 73 80 fractured 37 10000 80 90 fractured 38 10000 74 80 fractured 39 10000 69 70 fractured 40 15000 76 80 fractured 41 15000 71 85 fractured 42 15000 62 65 fractured 43 15000 73 75 fractured 44 15000 73 75 fractured 45 15000 66 70 fractured

TABLE 22 Bed Right side of Test diameter Expression ΔYS Test number [mm] (6) [MPa] result Remarks 46 7500 67 40 Not Example fractured 47 7500 66 10 Not fractured 48 7500 66 40 Not fractured 49 7500 65 30 Not fractured 50 7500 64 15 Not fractured 51 7500 68 50 Not fractured 52 7500 66 63 Not fractured 53 7500 66 60 Not fractured 54 9000 64 62 Not fractured 55 10000 67 64 Not fractured 56 10000 66 10 Not fractured 57 10000 61 49 Not fractured 58 15000 64 43 Not fractured 59 15000 68 0 Not fractured 60 15000 67 65 Not fractured 61 15000 63 5 Not fractured 62 15000 66 5 Not fractured 63 15000 64 50 Not fractured 64 15000 64 63 Not fractured 65 15000 68 43 Not fractured

TABLE 23 Bed Right side of Test diameter Expression ΔYS Test number [mm] (6) [MPa] result Remarks 66 7500 66 70 fractured Comparative 67 7500 64 65 fractured example 68 7500 61 65 fractured 69 7500 68 73 fractured 70 7500 66 70 fractured 71 7500 63 72 fractured 72 7500 66 68 fractured 73 10000 66 79 fractured 74 10000 64 70 fractured 75 10000 62 80 fractured 76 15000 64 68 fractured 77 15000 60 70 fractured 78 15000 64 71 fractured 79 15000 63 78 fractured 80 15000 64 84 fractured 81 15000 63 74 fractured

TABLE 24 Bed Right side of Test diameter Expression ΔYS Test number [mm] (6) [MPa] result Remarks 82 7500 64 2 Not Example fractured 83 7500 62 65 Not fractured 84 7500 59 52 Not fractured 85 7500 64 13 Not fractured 86 10000 64 50 Not fractured 87 10000 62 55 Not fractured 88 15000 60 22 Not fractured 89 15000 64 5 Not fractured 90 15000 57 18 Not fractured 91 15000 68 43 Not fractured 92 7500 62 81 fractured Comparative 93 7500 58 70 fractured example 94 7500 59 65 fractured 95 7500 60 83 fractured 96 7500 66 68 fractured 97 10000 64 70 fractured 98 10000 62 91 fractured 99 15000 64 69 fractured 100 15000 60 64 fractured 101 15000 62 68 fractured 102 15000 58 76 fractured 103 7500 59 55 Not Example fractured 104 10000 62 50 Not fractured 105 15000 58 19 Not fractured

TABLE 25 Bed Right side of Test diameter Expression ΔYS Test number [mm] (2) [MPa] result Remarks 106 15000 83 36 Not Example fractured 107 15000 80 65 Not fractured 108 15000 74 30 Not fractured 109 15000 66 70 fractured Comparative 110 15000 64 78 fractured example 111 15000 76 50 Not Example fractured 112 15000 69 20 Not fractured 113 15000 76 75 Not fractured 114 15000 76 5 Not fractured 115 15000 76 61 Not fractured 116 15000 69 75 fractured Comparative 117 15000 73 80 fractured example 118 15000 69 80 fractured 119 15000 67 74 fractured

TABLE 26 Bed Right side of Test diameter Expression ΔYS Test number [mm] (6) [MPa] result Remarks 120 10000 66 5 Not Example fractured 121 10000 65 47 Not fractured 122 10000 66 71 fractured Comparative example

TABLE 27 Bed Right side of Test diameter Expression ΔYS Test number [mm] (2) [MPa] result Remarks 123 15000 78 25 Not Example fractured 124 15000 71 10 Not fractured 125 15000 70 6 Not fractured 126 15000 76 33 Not fractured 127 15000 77 111 fractured Comparative example

TABLE 28 Right Bed Produc- side of Test diameter tion Expres- ΔYS Test number [mm] number sion (2) [MPa] result Remarks 128 7500 X + 1 76 28 Not Example X + 3 fractured 129 10000 Y + 1 81 40 Not Y + 2 fractured 130 15000 Z + 1 85 14 Not Z + 4 fractured 

1. A pipeline comprising a plurality of weld zones where ends of a plurality of steel pipes are joined by welding, wherein the plurality of the steel pipes is produced from a plurality of charges of molten steel having one or more steel compositions; a yield point elongation is not present on a stress-strain curve that is obtained when stress is applied in a longitudinal direction of each of the steel pipes; t which is a thickness of each of the steel pipes in units of mm and D which is an average pipe outside-diameter in units of mm satisfy a following Expression 1; and in the plurality of the weld zones, ΔYS which is a yield strength difference between one steel pipe and the other steel pipe that are welded to each other in units of MPa, and YR which represents a yield ratio that is a ratio of the yield strength to a tensile strength of a pipe having a low yield strength out of the one steel pipe and the other steel pipe, satisfy a following Expression 2: t/D×100≦6  (1) ΔYS≦−1.75×YR+230  (2).
 2. The pipeline according to claim 1, further comprising, as the steel compositions, by mass %, C: 0.04% or more and 0.15% or less, Mn: 1.0% or more and 1.75% or less, Nb: 0.005% or more and 0.10% or less, Ti: 0.005% or more and 0.02% or less, Al: 0.001% or more and 0.06% or less, Si: limited to 0.4% or less, P: limited to 0.015% or less, S: limited to 0.005% or less, N: limited to 0.007% or less, and a balance consisting of Fe and unavoidable impurities, wherein a ΔCeq value which is an absolute value of a difference of Ceq values expressed by a following Expression 3 between the one steel pipe and the other steel pipe is 0.045% or less, and the tensile strength of the plurality of the steel pipes is 450 MPa to 850 MPa or less, Ceq=[C]+[Mn]/6  (3) wherein [C], and [Mn] represent amounts of C and Mn by mass %.
 3. The pipeline according to claim 2, further comprising, as the steel compositions, by mass %, one or more of, Cu: 0.1% or more and 1.0% or less, Ni: 0.1% or more and 1.0% or less, Cr: 0.1% or more and 1.0% or less, Mo: 0.05% or more and 0.3% or less, and V: 0.01% or more and 0.1% or less, wherein the ΔCeq value is expressed by an Expression 4, Ceq=[C]+[Mn]/6+([Ni]+[Cu])/15+([Cr]+[Mo]+[V])/5  (4) wherein [C], [Mn], [Ni], [Cu], [Cr], [Mo], and [V] represent amounts of C, Mn, Ni, Cu, Cr, Mo, and V by mass %.
 4. A pipeline comprising a plurality of weld zones where ends of a plurality of steel pipes are joined by welding, wherein: the plurality of the steel pipes are produced from a plurality of charges of molten steel having one or more steel compositions; a yield point elongation is present on a stress-strain curve that is obtained when stress is applied in a longitudinal direction of each of the steel pipes; t which is a thickness of each of the steel pipes in units of mm and D which is an average pipe outside-diameter in units of mm satisfy a following Expression 5; and in the plurality of the weld zones, LYS which is a yield strength difference between one steel pipe and the other steel pipe that are welded to each other in units of MPa, and YR which represents a yield ratio that is a ratio of the yield strength to a tensile strength of a pipe having a low yield strength out of the one steel pipe and the other steel pipe, satisfy a following Expression 6: t/D×100≦6  (5) ΔYS≦−0.69×YR+125  (6).
 5. The pipeline according to claim 4, further comprising, as the steel compositions, by mass %, C: 0.04% or more and 0.15% or less, Mn: 1.0% or more and 1.75% or less, Nb: 0.005% or more and 0.10% or less, Ti: 0.005% or more and 0.02% or less, Al: 0.001% or more and 0.06% or less, Si: limited to 0.4% or less, P: limited to 0.015% or less, S limited to 0.005% or less, N: limited to 0.007% or less, and a balance consisting of Fe and unavoidable impurities, wherein a ΔCeq value which is an absolute value of a difference of Ceq values expressed by a following Expression 7 between the one steel pipe and the other steel pipe is 0.045% or less, the tensile strength of the plurality of the steel pipes is 450 MPa to 850 MPa or less, and front and rear surfaces of the plurality of the steel pipes are coated with thermosetting resin, Ceq=[C]+[Mn]/6  (7) wherein [C], and [Mn] represent amounts of C and Mn by mass %.
 6. The pipeline according to claim 5, further comprising, as the steel compositions, by mass %, one or more of, Cu: 0.1% or more and 1.0% or less, Ni: 0.1% or more and 1.0% or less, Cr: 0.1% or more and 1.0% or less, Mo: 0.05% or more and 0.3% or less, and V: 0.01% or more and 0.1% or less, wherein the ΔCeq value is expressed by Expression 8, Ceq=[C]+[Mn]/6++[Cu])/15+([Cr]+[Mo]+[V])/5  (8) wherein [C], [Mn], [Ni], [Cu], [Cr], [Mo], and [V] represent amounts of C, Mn, Ni, Cu, Cr, Mo, and V by mass %.
 7. The pipeline according to claim 4, further comprising, as the steel compositions, by mass %, C: 0.04% or more and 0.15% or less, Mn: 1.0% or more and 1.75% or less, Nb: 0.005% or more and 0.10% or less, Ti: 0.005% or more and 0.02% or less, Al: 0.001% or more and 0.06% or less, Si: limited to 0.4% or less, P: limited to 0.015% or less, S: limited to 0.005% or less, N: limited to 0.007% or less, and a remainder consisting of Fe and unavoidable impurities, wherein a ΔCeq value which is an absolute value of a difference of Ceq values expressed by a following Expression 9 between the one steel pipe and the other steel pipe is 0.045% or less, and the tensile strength of the plurality of the steel pipes is 450 MPa to 850 MPa or less Ceq=[C]+[Mn]/6  (9) wherein [C], and [Mn] represent amounts of C and Mn by mass %.
 8. The pipeline according to claim 7, further comprising, as the steel compositions, by mass %, one or more of, Cu: 0.1% or more and 1.0% or less, Ni: 0.1% or more and 1.0% or less, Cr: 0.1% or more and 1.0% or less, Mo: 0.05% or more and 0.3% or less, and V: 0.01% or more and 0.1% or less, wherein the ΔCeq value is expressed by Expression 10, Ceq=[C]+[Mn]/6+([Ni]+[Cu])/15+([Cr]+[Mo]+[V])/5  (10) wherein [C], [Mn], [Ni], [Cu], [Cr], [Mo], and [V] represent amounts of C, Mn, Ni, Cu, Cr, Mo, and V by mass %.
 9. A method of producing the pipeline according to claim 1, comprising: a first yield strength measuring process in which the yield strength of the plurality of the steel pipes is measured; and a first welding process in which steel pipes in which the ΔYS satisfies the Expression 2 are welded.
 10. A method of producing the pipeline according to claim 1, comprising: a first assigning process in which production numbers capable of specifying each of the steel pipes are assigned to the plurality of the steel pipes in order of rolling; and a second welding process in which steel pipes produced from the same molten steel and the same hot-rolled coil and having a difference between the production numbers of 1 or more and 5 or less are welded.
 11. A method of producing the pipeline according to claim 4, comprising: a second yield strength measuring process in which the yield strength of the plurality of the steel pipes is measured; and a third welding process in which steel pipes in which the ΔYS satisfies the Expression 6 are welded.
 12. A method of producing the pipeline according to claim 4, comprising: a second assigning process in which production numbers capable of specifying each of the steel pipes are assigned to the plurality of the steel pipes in order of rolling; and a forth welding process in which steel pipes produced from the same molten steel and having a difference between the production numbers of 1 or more and 5 or less are welded. 